EP3878033B1 - Elektroaktive materialien für metall-ionen-batterien - Google Patents

Elektroaktive materialien für metall-ionen-batterien Download PDF

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EP3878033B1
EP3878033B1 EP19804801.9A EP19804801A EP3878033B1 EP 3878033 B1 EP3878033 B1 EP 3878033B1 EP 19804801 A EP19804801 A EP 19804801A EP 3878033 B1 EP3878033 B1 EP 3878033B1
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range
silicon
particulate material
porous carbon
carbon framework
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French (fr)
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EP3878033A1 (de
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Charles A. MASON
Richard Gregory Taylor
James Farrell
William James Macklin
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Nexeon Ltd
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Nexeon Ltd
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    • H—ELECTRICITY
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    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/362—Composites
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    • H01M10/052—Li-accumulators
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    • H01M10/052—Li-accumulators
    • H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
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    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
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    • H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
    • H01M4/386—Silicon or alloys based on silicon
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    • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
    • H01M4/583—Carbonaceous material, e.g. graphite-intercalation compounds or CFx
    • H01M4/587—Carbonaceous material, e.g. graphite-intercalation compounds or CFx for inserting or intercalating light metals
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    • H01M4/0471—Processes of manufacture in general involving thermal treatment, e.g. firing, sintering, backing particulate active material, thermal decomposition, pyrolysis
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    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries

Definitions

  • This invention relates in general to electroactive materials that are suitable for use in electrodes for rechargeable metal-ion batteries, and more specifically to particulate materials having high electrochemical capacities that are suitable for use as anode active materials in rechargeable metal-ion batteries.
  • Rechargeable metal-ion batteries are widely used in portable electronic devices such as mobile telephones and laptops and are finding increasing application in electric or hybrid vehicles.
  • Rechargeable metal-ion batteries generally comprise an anode layer, a cathode layer, an electrolyte to transport metal ions between the anode and cathode layers, and an electrically insulating porous separator disposed between the anode and the cathode.
  • the cathode typically comprises a metal current collector provided with a layer of metal ion containing metal oxide based composite
  • the anode typically comprises a metal current collector provided with a layer of an electroactive material, defined herein as a material which is capable of inserting and releasing metal ions during the charging and discharging of a battery.
  • cathode and anode are used herein in the sense that the battery is placed across a load, such that the cathode is the positive electrode and the anode is the negative electrode.
  • metal ions are transported from the metal-ion-containing cathode layer via the electrolyte to the anode and are inserted into the anode material.
  • battery is used herein to refer both to a device containing a single anode and a single cathode and to devices containing a plurality of anodes and/or a plurality of cathodes.
  • lithium-ion batteries have already provided a substantial improvement when compared to other battery technologies, but there remains scope for further development.
  • commercial lithium-ion batteries have largely been limited to the use of graphite as an anode active material.
  • graphite When a graphite anode is charged, lithium intercalates between the graphite layers to form a material with the empirical formula Li x C 6 (wherein x is greater than 0 and less than or equal to 1). Consequently, graphite has a maximum theoretical capacity of 372 mAh/g in a lithium-ion battery, with a practical capacity that is somewhat lower (ca. 340 to 360 mAh/g).
  • Other materials such as silicon, tin and germanium, are capable of intercalating lithium with a significantly higher capacity than graphite but have yet to find widespread commercial use due to difficulties in maintaining sufficient capacity over numerous charge/discharge cycles.
  • Silicon in particular has been identified as a promising alternative to graphite for the manufacture of rechargeable metal-ion batteries having high gravimetric and volumetric capacities because of its very high capacity for lithium (see, for example, Insertion Electrode Materials for Rechargeable Lithium Batteries, Winter, M. et al. in Adv. Mater. 1998, 10, No. 10 ).
  • silicon At room temperature, silicon has a theoretical maximum specific capacity in a lithium-ion battery of about 3,600 mAh/g (based on Li 15 Si 4 ).
  • the use of silicon as an anode material is complicated by large volumetric changes on charging and discharging.
  • WO 2007/083155 discloses that improved capacity retention may be obtained through the use of silicon particles having high aspect ratio, i.e. the ratio of the largest dimension to the smallest dimension of the particle.
  • electroactive materials such as silicon may be deposited within the pores of a porous carrier material, such as an activated carbon material.
  • a porous carrier material such as an activated carbon material.
  • These composite materials provide some of the beneficial charge-discharge properties of nanoscale silicon particles while avoiding the handling difficulties of nanoparticles.
  • Guo et al. discloses a silicon-carbon composite material in which a porous carbon substrate provides an electrically conductive framework with silicon nanoparticles deposited within the pore structure of the substrate with uniform distribution. SEI formation over the initial charging cycles is confined to the remaining pore volume such that the remaining silicon is not exposed to the electrolyte in subsequent charging cycles. It is shown that the composite material has improved capacity retention over multiple charging cycles, however the initial capacity of the composite material in mAh/g is significantly lower than for silicon nanoparticles.
  • JP2003100284 discloses an active material comprising a carbon-based scaffold with small pores branching off from a few larger pores.
  • An electroactive material e.g. silicon
  • An electroactive material is indiscriminately located on the walls of both large and small pores and on the external surface of the carbon-based scaffold.
  • US 2014/272592 relates to composite carbon materials, methods for making the same and devices containing the same.
  • the present invention is based on the observation that the performance of composite materials comprising a porous carbon framework and silicon as an electroactive material located within the porous carbon framework can be optimised by using porous carbon frameworks with specific pore structures and a controlled ratio of silicon to the available pore volume.
  • the invention provides a particulate material comprising a plurality of composite particles, wherein the composite particles comprise:
  • the invention therefore relates to a particulate material in which the porous carbon framework has relatively high total volume of micropores and mesopores, with pores having a diameter of no more than 5 nm constituting at least 50% of the total pore volume.
  • P 1 as used herein relates to the pore volume of the porous carbon framework when measured in isolation, i.e. in the absence of silicon or any other material occupying the pores of the porous carbon framework.
  • Elemental silicon is located in the micropores and/or mesopores in the form of a plurality of nanoscale silicon domains.
  • nanoscale silicon domain refers to a nanoscale body of silicon that is located within the pores of the porous carbon framework. At least a portion of the nanoscale silicon domains occupy at least a portion of the mesopores and/or micropores having a diameter less than the PD 50 pore diameter and therefore have a dimension of no more than 5 nm.
  • the weight ratio of silicon to the porous carbon framework is correlated to the total micropore/mesopore volume by the ratio [0.5 ⁇ P 1 to 1.3 ⁇ P 1 ] : 1.
  • the weight ratio of silicon based on the value of P 1 , the percentage volumetric occupancy of the pore volume by silicon is controlled within specific limits. Put another way, where the weight ratio of silicon to the porous carbon framework is in the range of [0.5 ⁇ P 1 to 1.3 ⁇ P 1 ] : 1, the volume of silicon in the composite particles is equivalent to approximately 20%-55% of the total micropore/mesopore volume of the porous carbon framework.
  • the invention therefore relates in general terms to a particulate material in which silicon partially occupies the pores of a highly porous carbon framework in which the pore volume is largely in the form of small mesopores and/or micropores. It has been found that this particle architecture provides an electroactive material with a high gravimetric and volumetric capacity on lithiation and which demonstrates a unique ability to accommodate the expansion of silicon and therefore high reversible capacity retention over multiple charge-discharge cycles.
  • the exceptional reversible capacity retention of the inventive particulate material is a function of the high porosity of the porous carbon framework, the high proportion of small mesopores and/or micropores in the porous carbon framework and the controlled loading of silicon in the composite relative to the total mesopore/micropore volume.
  • nanoscale silicon domains within small mesopores and/or micropores firstly provides fine silicon structures which are able to lithiate and delithiate without excessive structural stress. It is believed that these very fine silicon domains have a lower resistance to elastic deformation and higher fracture resistance than larger silicon structures.
  • the unoccupied pore volume of the porous carbon framework is able to accommodate a substantial amount of silicon expansion internally. More specifically, it is believed that the highly microporous carbon framework is able to deform elastically with reduced rate of fracture due to thin pore walls and the tensile fracture strength of the framework is very high.
  • the low resistance of the silicon to elastic deformation therefore works in synergy with the high relative modulus of carbon to drive silicon expansion into the pore volume of the porous carbon framework.
  • the amount of external expansion is limited due to the silicon expansion that is accommodated internally.
  • the fine pore structure of the porous carbon framework is able to deform without fracturing.
  • strain on the porous carbon framework and the silicon domains is limited to a level which is tolerated over large numbers of charge-discharge cycles without substantial loss of capacity.
  • the high total porosity of the porous carbon framework not only provides for high volumetric loadings of silicon, but also ensures that the porous carbon framework is sufficiently resilient to withstand repeated volume changes over multiple charge-discharge cycles.
  • the silicon in the composite particles has electrochemical performance that is comparable to that of fine silicon nanoparticles but without the disadvantages of excessive SEI formation and poor dispersibility that make discrete silicon nanoparticles non-viable as an electrode material for commercial use.
  • the porous carbon framework suitably comprises a three-dimensionally interconnected open pore network comprising a combination of micropores and/or mesopores and optionally a minor volume of macropores.
  • micropore is used herein to refer to pores of less than 2 nm in diameter
  • mesopore is used herein to refer to pores of 2-50 nm in diameter
  • macropore is used to refer to pores of greater than 50 nm diameter.
  • references herein to the volume of micropores, mesopores and macropores in the porous carbon framework, and any references to the distribution of pore volume within the porous carbon framework, refer to the internal pore volume of the porous carbon framework taken in isolation (i.e. in the absence of any silicon or other materials occupying some or all of the pore volume).
  • the porous carbon framework is characterised by a high pore volume in the form of micropores and/or mesopores.
  • the total volume of micropores and mesopores i.e. the total pore volume in the range of 0 to 50 nm
  • P 1 cm 3 /g wherein P 1 represents a dimensionless natural number having a value of at least 0.7.
  • the value of P 1 is also used to correlate the available pore volume in the porous carbon framework and the weight ratio of silicon to the porous carbon framework as set out above.
  • the value of P 1 is at least 0.75, or at least 0.8, or at least 0.85.
  • the value of P 1 may be at least 0.9, or at least 0.95, or at least 1, for example at least 1.05, at least 1.1, at least 1.15, or at least 1.2.
  • the use of a high porosity carbon framework is advantageous since it allows a larger amount of silicon to be accommodated within the pore structure, and it has been found that high porosity carbon frameworks in which the pore volume is predominantly in the form of micropores and/or smaller mesopores have sufficient strength to accommodate the volumetric expansion of the silicon without fracturing or otherwise degrading the porous carbon framework.
  • the internal pore volume of the porous carbon framework is suitably capped at a value at which increasing fragility of the porous carbon framework outweighs the advantage of increased pore volume accommodating a larger amount of silicon.
  • the value of P 1 may be no more than 2.5. However, more preferably, the value of P 1 may be no more than 2.2, or no more than 2, or no more than 1.8, or no more than 1.6, or no more than 1.5, or no more than 1.4, or no more than 1.3, or no more than 1.2, or no more than 1.1, or no more than 1.0, or no more than 0.9.
  • the value of P 1 is no more than 1.2, or no more than 1.1, or no more than 1.0, or no more than 0.9.
  • the value of P 1 may be, for instance, in the range from 0.8 to 2.2, or in the range from 0.85 to 2.2, or in the range from 0.9 to 2.2, or in the range from 0.95 to 2.2, or in the range from 1 to 2.2, or in the range from 1.05 to 2.2, or in the range from 1.1 to 2.2, or in the range from 0.8 to 2, or in the range from 0.85 to 2, or in the range from 0.9 to 2, or in the range from 0.95 to 2, or in the range from 1 to 2, or in the range from 1.05 to 2, or in the range from 1.1 to 2, or in the range from 0.8 to 1.9, or in the range from 0.85 to 1.9, or in the range from 0.9 to 1.9, or in the range from 0.95 to 1.9, or in the range from 1 to 1.9, or in the range from 1.05 to 1.9, or in the range from 1.1 to 1.9, or in the range from 0.8 to 1.8, or in the range from 0.85 to 1.8, or in the range from 0.85 to
  • the value of P 1 may be, for instance, in the range from 0.7 to 1.5, or in the range from 0.75 to 1.4, or in the range from 0.7 to 1.3, or in the range from 0.75 to 1.3, or in the range from 0.7 to 1.2, or in the range from 0.75 to 1.2, or in the range from 0.7 to 1, or in the range from 0.75 to 1, or in the range from 0.7 to 0.9, or in the range from 0.75 to 0.9.
  • the PD 50 pore diameter of the porous carbon framework is less than 5 nm.
  • the term "PD 50 pore diameter" as used herein refers to the volume-based median pore diameter, based on the total volume of micropores and mesopores (i.e. the pore diameter below which 50% of the total micropore and mesopore volume, represented by P 1 , is found). Therefore, in accordance with the invention, at least 50% of the total volume of micropores and mesopores is in the form of pores having a diameter of less than 5 nm.
  • PD n pore diameter refers to the volume-based nth percentile pore diameter, based on the total volume of micropores and mesopores.
  • D 90 pore diameter refers to the pore diameter below which 90% of the total micropore and mesopore volume, represented by P 1 , is found).
  • any macropore volume (pore diameter greater than 50 nm) is not taken into account for the purpose of determining PD n values.
  • the PD 50 pore diameter of the porous carbon framework is preferably no more than 4 nm, or no more than 3 nm, or no more than 2.5 nm, or no more than 2 nm.
  • the PD 50 pore diameter of the porous carbon framework is at least 0.8 nm, or at least 1 nm, or at least 1.2 nm.
  • the PD 60 pore diameter of the porous carbon framework is preferably no more than 5 nm, or no more than 4 nm, or no more than 3 nm, or no more than 2.5 nm, or no more than 2 nm, or no more than 1.5 nm.
  • the PD 70 pore diameter of the porous carbon framework is preferably no more than 5 nm, or no more than 4 nm, or no more than 3 nm, or no more than 2.5 nm, or no more than 2 nm.
  • the PD 80 pore diameter of the porous carbon framework is preferably no more than 5 nm, or no more than 4 nm, or no more than 3 nm, or no more than 2.5 nm, or no more than 2 nm.
  • the volume of larger mesopores in the porous carbon framework is preferably limited such that the PD 90 pore diameter is no more than 20 nm, or no more than 15 nm, or no more than 12 nm, or no more than 10 nm, or no more than 8 nm, or no more than 6 nm, or no more than 5 nm, or no more than 4 nm, or no more than 3 nm, or no more than 2.5 nm, or no more than 2 nm.
  • the PD 95 pore diameter is no more than 20 nm, or no more than 15 nm, or no more than 12 nm, or no more than 10 nm.
  • the porous carbon framework may be one in which PD 50 is no more than 5 nm and PD 90 is no more than 20 nm, or one in which PD 50 is no more than 4 nm and PD 90 is no more than 15 nm, or one in which PD 50 is no more than 3 nm and PD 90 is no more than 12 nm, or one in which PD 50 is no more than 3 nm and PD 90 is no more than 10 nm, or one in which PD 50 is no more than 2.5 nm and PD 90 is no more than 10 nm, or one in which PD 50 is no more than 2 nm and PD 90 is no more than 8 nm, or one in which PD 50 is no more than 2 nm and PD 90 is no more than 6 nm, or one in which PD 50 is no more than 1.5 nm and PD 90 is no more than 6 nm.
  • the porous carbon framework may be one in which PD 50 is from 1 to 5 nm and PD 90 is from 3 to 20 nm, or one in which PD 50 is from 1 to 4 nm and PD 90 is from 3 to 15 nm, or one in which PD 50 is from 1 to 3 nm and PD 90 is from 3 to 12 nm, or one in which PD 50 is from 1 to 3 nm and PD 90 is from 3 to 10 nm, or one in which PD 50 is from 1 to 2.5 nm and PD 90 is from 3 to 10 nm, or one in which PD 50 is from 1 to 2 nm and PD 90 is from 3 to 8 nm, or one in which PD 50 is from 1 to 2 nm and PD 90 is from 3 to 6 nm, or one in which PD 50 is from 1 to 2 nm and PD 90 is from 3 to 6 nm.
  • pores having a diameter in the range of 10 to 50 nm may optionally constitute at least 1%, at least 2%, at least 5% or at least 10% of the total micropore and mesopore volume of the porous carbon framework.
  • the volumetric ratio of micropores to mesopores in the porous carbon framework may range in principle from 100:0 to 0:100.
  • the volumetric ratio of micropores to mesopores is from 90:10 to 55:45, or from 90:10 to 60:40, or from 85:15 to 65:35.
  • the pore size distribution of the porous carbon framework may be monomodal, bimodal or multimodal.
  • the term "pore size distribution” relates to the distribution of pore size relative to the cumulative total internal pore volume of the porous carbon framework.
  • a bimodal or multimodal pore size distribution may be preferred since close proximity between the pores up to 5 nm in diameter and pores of larger diameter provides the advantage of efficient ionic transport through the porous network to the silicon. Accordingly, the particulate material has high ionic diffusivity and therefore improved rate performance.
  • the porous carbon framework has a bimodal or multimodal pore size distribution including at least one peak at less than 2 nm and at least one peak in the range from 5 to 50 nm, preferably with a local minimum in the pore size distribution in the range from 5 to 20 nm. More preferably, the porous carbon framework has a bimodal or multimodal pore size distribution including at least one peak at less than 2 nm and at least one peak in the range from 10 to 40 nm, preferably with a local minimum in the pore size distribution in the range from 5 to 15 nm.
  • a bimodal or multimodal pore size distribution includes a peak pore size in the micropore range and a peak pore size in the mesopore size range which differ from one another by a factor of from 5 to 20, more preferably by a factor of about 10.
  • the porous carbon framework may have a bimodal pore size distribution including a peak at a pore size of 2 nm and a peak at a pore size of 20 nm.
  • the total volume of micropores and mesopores and the pore size distribution of micropores and mesopores are determined using nitrogen gas adsorption at 77 K down to a relative pressure p/po of 10 -6 using quenched solid density functional theory (QSDFT) in accordance with standard methodology as set out in ISO 15901-2 and ISO 15901-3.
  • Nitrogen gas adsorption is a technique that characterizes the porosity and pore diameter distributions of a material by allowing a gas to condense in the pores of a solid. As pressure increases, the gas condenses first in the pores of smallest diameter and the pressure is increased until a saturation point is reached at which all of the pores are filled with liquid.
  • the nitrogen gas pressure is then reduced incrementally, to allow the liquid to evaporate from the system.
  • Suitable instruments for the measurement of pore volume and pore size distributions by nitrogen gas adsorption include the TriStar II and TriStar II Plus porosity analyzers, which are available from Micromeritics Instrument Corporation, USA, and the Autosorb IQ porosity analyzers, which are available from Quantachrome Instruments.
  • Nitrogen gas adsorption is effective for the measurement of pore volume and pore size distributions for pores having a diameter up to 50 nm, but is less reliable for pores of much larger diameter.
  • nitrogen adsorption is therefore used to determine pore volumes and pore size distributions only for pores having a diameter up to and including 50 nm.
  • the value of P 1 is determined by taking into account only pores of diameter up to and including 50 nm (i.e. only micropores and mesopores), and the values of PD n are likewise determined relative to the total volume of micropores and mesopores only.
  • the porous carbon framework comprises macropores
  • the volume of pores in the range of greater than 50 nm and up to 100 nm is identified herein with the value of P 2 cm 3 /g and is measured by mercury porosimetry.
  • the value of P 2 relates to the pore volume of the porous carbon framework when measured in isolation, i.e. in the absence of silicon or any other material occupying the pores of the porous carbon framework.
  • the value of P 2 takes into account only pores having a diameter of from greater than 50 nm up to and including 100 nm, i.e. it includes only the volume of macropores up to 100 nm in diameter. Any pore volume measured by mercury porosimetry at pore sizes of 50 nm or below is disregarded for the purposes of determining the value of P 2 (as set out above, nitrogen adsorption is used to characterize the mesopores and micropores). Pore volume measured by mercury porosimetry above 100 nm is assumed for the purposes of the invention to be inter-particle porosity and is also not take into account when determining the value of P 2 .
  • Mercury porosimetry is a technique that characterizes the porosity and pore diameter distributions of a material by applying varying levels of pressure to a sample of the material immersed in mercury. The pressure required to intrude mercury into the pores of the sample is inversely proportional to the size of the pores. Values obtained by mercury porosimetry as reported herein are obtained in accordance with ASTM UOP578-11, with the surface tension ⁇ taken to be 480 mN/m and the contact angle ⁇ taken to be 140° for mercury at room temperature. The density of mercury is taken to be 13.5462 g/cm 3 at room temperature.
  • the volume of macropores (and therefore the value of P 2 ) is preferably small as compared to the volume of micropores and mesopores (and therefore the value of P 1 ). While a small fraction of macropores may be useful to facilitate electrolyte access into the pore network, the advantages of the invention are obtained substantially by accommodating silicon in micropores and smaller mesopores.
  • the total volume of macropores in the porous carbon framework is P 2 cm 3 /g as measured by mercury porosimetry, wherein P 2 preferably has a value of no more than 0.2 ⁇ P 1 , or no more than 0.1 ⁇ P 1 , or no more than 0.05 ⁇ P 1 , or no more than 0.02 ⁇ P 1 , or no more than 0.01 ⁇ P 1 , or no more than 0.005 ⁇ P 1 .
  • P 2 has a value of no more than 0.3, or no more than 0.25, or no more than 0.20, or no more than 0.15, or no more than 0.1, or no more than 0.05.
  • a small pore volume fraction in the macropore range may be advantageous to facilitate electrolyte access to the silicon.
  • the open pore network optionally includes a hierarchical pore structure, i.e. a pore structure in which there is a degree of ordering of pore sizes, with smaller pores branching from larger pores.
  • a hierarchical pore structure i.e. a pore structure in which there is a degree of ordering of pore sizes, with smaller pores branching from larger pores.
  • Porosity values (P 1 and P 2 ) as specified herein shall be understood as referring to the volume of open pores, i.e. pores that are accessible to a fluid from the exterior of the porous carbon framework. Fully enclosed pores which cannot be identified by nitrogen adsorption or mercury porosimetry shall not be taken into account herein when specifying porosity values. Likewise, any pore volume located in pores that are so small as to be below the limit of detection by nitrogen adsorption is not taken into account for determining the value of P 1 .
  • the porous carbon framework may comprise crystalline carbon or amorphous carbon, or a mixture of amorphous and crystalline carbon.
  • the porous carbon framework may be either a hard carbon or soft carbon framework and may suitably be obtained by known procedures involving the the pyrolysis of polymers.
  • hard carbon refers to a disordered carbon matrix in which carbon atoms are found predominantly in the sp 2 hybridised state (trigonal bonds) in nanoscale polyaromatic domains.
  • the polyaromatic domains are cross-linked with a chemical bond, e.g. a C-O-C bond. Due to the chemical cross-linking between the polyaromatic domains, hard carbons cannot be converted to graphite at high temperatures.
  • Hard carbons have graphite-like character as evidenced by the large G-band (-1600 cm -1 ) in the Raman spectrum. However, the carbon is not fully graphitic as evidenced by the significant D-band (-1350 cm -1 ) in the Raman spectrum.
  • soft carbon also refers to a disordered carbon matrix in which carbon atoms are found predominantly in the sp 2 hybridised state (trigonal bonds) in polyaromatic domains having dimensions in the range of 5-200 nm.
  • the polyaromatic domains in soft carbons are associated by intermolecular forces but are not cross-linked with a chemical bond. This means that they will graphitise at high temperature.
  • the porous carbon framework preferably comprises at least 50% sp 2 hybridised carbon as measured by XPS.
  • the porous carbon framework may suitably comprise from 50% to 98% sp 2 hybridised carbon, from 55% to 95% sp 2 hybridised carbon, from 60% to 90% sp 2 hybridised carbon, or from 70% to 85% sp 2 hybridised carbon.
  • a variety of different materials may be used to prepare suitable porous carbon frameworks.
  • organic materials include plant biomass including lignocellulosic materials (such as coconut shells, rice husks, wood etc.) and fossil carbon sources such as coal.
  • polymeric materials which form porous carbon frameworks on pyrolysis include phenolic resins, novolac resins, pitch, melamines, polyacrylates, polystyrenes, polyvinylalcohol (PVA), polyvinylpyrrolidone (PVP), and various copolymers comprising monomer units of acrylates, styrenes, ⁇ -olefins, vinyl pyrrolidone and other ethylenically unsaturated monomers.
  • PVA polyvinylalcohol
  • PVP polyvinylpyrrolidone
  • a variety of different hard carbon materials are available in the art depending on the starting material and the conditions of the pyrolysis process.
  • the porous carbon framework may undergo a chemical or gaseous activation process to increase the volume of mesopores and micropores.
  • a suitable activation process comprises contacting pyrolysed carbon with one or more of oxygen, steam, CO, CO 2 and KOH at a temperature in the range from 600 to 1000°C.
  • Mesopores can also be obtained by known templating processes, using extractable pore formers such as MgO and other colloidal or polymer templates which can be removed by thermal or chemical means post pyrolysis or activation.
  • the porous carbon framework preferably has a BET surface area of at least 750 m 2 /g, or at least 1,000 m 2 /g, or at least 1,250 m 2 /g, or at least 1,500 m 2 /g.
  • BET surface area should be taken to refer to the surface area per unit mass calculated from a measurement of the physical adsorption of gas molecules on a solid surface, using the Brunauer-Emmett-Teller theory, in accordance with ISO 9277.
  • the BET surface area of the conductive porous particle framework is no more than 4,000 m 2 /g, or no more than 3,500 m 2 /g, or no more than 3,250 m 2 /g, or no more than 3,000 m 2 /g.
  • the amount of silicon in the composite particles of the invention is preferably selected such that no more than about 55% of the internal pore volume of the porous carbon framework is occupied by silicon (in the uncharged state).
  • the silicon occupies from about 25% to about 45% of the internal pore volume of the porous carbon framework, more preferably from about 25% to 40% of the internal pore volume of the porous carbon framework.
  • the pore volume of the porous carbon framework is effective to accommodate expansion of the silicon during charging and discharging, but avoids excess pore volume which does not contribute to the volumetric capacity of the particulate material.
  • the amount of silicon is also not so high as to impede effective lithiation due to inadequate metal-ion diffusion rates or due to inadequate expansion volume resulting in mechanical resistance to lithiation.
  • the amount of silicon in the porous carbon framework can be correlated to the available pore volume by the requirement that the weight ratio of silicon to the porous carbon framework is in the range from [0.5 ⁇ P 1 to 1.3 ⁇ P 1 ] : 1. This relationship takes into account the density of silicon and the pore volume of the porous carbon framework to define a weight ratio of silicon at which the pore volume is around 20% to 55% occupied.
  • the weight ratio of silicon to the porous carbon framework is in the range from [0.55 ⁇ P 1 to 1.1 ⁇ P 1 ] : 1, or in the range from [0.6 ⁇ P 1 to 1.1 ⁇ P 1 ]: 1, or in the range from [0.6 ⁇ P 1 to 1 ⁇ P 1 ] : 1, or in the range from [0.6 ⁇ P 1 to 0.95 ⁇ P 1 ] : 1, or in the range from [0.6 ⁇ P 1 to 0.9 ⁇ P 1 ] : 1, or in the range from [0.65 ⁇ P 1 to 0.9 ⁇ P 1 ] : 1, or in the range from [0.65 ⁇ P 1 to 0.85 ⁇ P 1 ] : 1, or in the range from [0.65 ⁇ P 1 to 0.8 ⁇ P 1 ] : 1, or in the range from [0.7 ⁇ P 1 to 0.8 ⁇ P 1 ] : 1.
  • the composite particles may include pores in which fully enclosed void space is capped by the silicon, such that electrolyte access into the void space is prevented.
  • At least 90 wt%, more preferably at least 95 wt%, even more preferably at least 98wt% of the silicon mass in the composite particles is located within the internal pore volume of the porous carbon framework such that there is no or very little silicon located on the external surfaces of the composite particles.
  • the particulate materials of the invention can be further characterised by their performance under thermogravimetric analysis (TGA) in air.
  • TGA thermogravimetric analysis
  • the determination of the amount of unoxidised silicon is derived from the characteristic TGA trace for these materials.
  • a mass increase at ca. 300-500 °C corresponds to initial oxidation of silicon to SiO 2 , and is followed by mass loss at ca. 500-600 °C as carbon is oxidised to CO 2 gas. Above ca. 600 °C, there is a further mass increase corresponding to the continued conversion of silicon to SiO 2 which increases toward an asymptotic value above 1000 °C as silicon oxidation goes to completion.
  • Z is the percentage of unoxidized silicon at 800 °C
  • M f is the mass of the sample at completion of oxidation
  • Msoo is the mass of the sample at 800 °C.
  • the temperature at which silicon is oxidised under TGA corresponds broadly to the length scale of the oxide coating on the silicon due to diffusion of oxygen atoms through the oxide layer being thermally activated.
  • the size of the silicon nanostructure and its location limit the length scale of the oxide coating thickness. Therefore it is understood that silicon deposited in micropores and mesopores will oxidise at a lower temperature than deposits of silicon on a particle surface due to the necessarily thinner oxide coating existing on these structures.
  • preferred materials according to the invention exhibit substantially complete oxidation of silicon at low temperatures consistent with the small length scale of silicon nanostructures that are located in micropores and smaller mesopores.
  • silicon oxidation at 800 °C is assumed to be silicon on the external surfaces of the porous carbon framework.
  • the silicon is preferably amorphous silicon. It is believed that amorphous silicon has better performance as an electroactive material.
  • the morphology of the silicon can be determined by known procedures using X-Ray Diffraction (XRD).
  • the volume of micropores and mesopores in the composite particles is no more than 0.15 ⁇ P 1 , or no more than 0.10 ⁇ P 1 , or no more than 0.05 ⁇ P 1 , or no more than 0.02 ⁇ P 1 .
  • the weight ratio of silicon to the porous carbon framework can be determined by elemental analysis. Elemental analysis is used to determine the weight percentages of both silicon and carbon in the composite particles. Optionally, the amounts of hydrogen, nitrogen and oxygen may also be determined by elemental analysis. Preferably, elemental analysis is also used to determine the weight percentage of carbon (and optionally hydrogen, nitrogen and oxygen) in the porous carbon framework alone. Determining the weight percentage of carbon in the in the porous carbon framework alone takes account of the possibility that the porous carbon framework contains a minor amount of heteroatoms within its molecular framework. Both measurements taken together allow the weight percentage of silicon relative to the entire porous carbon framework to be determined reliably.
  • the silicon content is preferably determined by ICP-OES (Inductively coupled plasma-optical emission spectrometry).
  • ICP-OES Inductively coupled plasma-optical emission spectrometry
  • a number of ICP-OES instruments are commercially available, such as the iCAP ® 7000 series of ICP-OES analyzers available from ThermoFisher Scientific.
  • the carbon content of the composite particles and of the porous carbon framework alone (as well as the hydrogen, nitrogen and oxygen content if required) are preferably determined by IR absorption.
  • a suitable instrument for determining carbon, hydrogen, nitrogen and oxygen content is the TruSpec ® Micro elemental analyser available from Leco Corporation.
  • the composite particles preferably have a low total oxygen content.
  • Oxygen may be present in the composite particles for instance as part of the porous carbon framework or as an oxide layer on any exposed silicon surfaces.
  • the total oxygen content of the composite particles is less than 15 wt%, more preferably less than 10 wt%, more preferably less than 5 wt%, for example less than 2 wt%, or less than 1 wt%, or less than 0.5 wt%.
  • the silicon may optionally comprise a minor amount of one or more dopants.
  • Suitable dopants include boron and phosphorus, other n-type or p-type dopants, nitrogen, or germanium.
  • the dopants are present in a total amount of no more than 2 wt% based on the total amount of silicon and the dopant(s).
  • particle diameter refers to the equivalent spherical diameter (esd), i.e. the diameter of a sphere having the same volume as a given particle, wherein the particle volume is understood to include the volume of any intra-particle pores.
  • D 50 and D 50 particle diameter refer to the volume-based median particle diameter, i.e. the diameter below which 50% by volume of the particle population is found.
  • D 10 and D 10 particle diameter refer to the 10th percentile volume-based particle diameter, i.e. the diameter below which 10% by volume of the particle population is found.
  • D 90 and “D 90 particle diameter” as used herein refer to the 90th percentile volume-based particle diameter, i.e. the diameter below which 90% by volume of the particle population is found.
  • D n used herein to define particle diameter distributions should be distinguished from the terminology “PD n” which is used herein, as described above, to define pore diameter distributions.
  • Particle diameters and particle size distributions can be determined by routine laser diffraction techniques in accordance with ISO 13320:2009.
  • Laser diffraction relies on the principle that a particle will scatter light at an angle that varies depending on the size the particle and a collection of particles will produce a pattern of scattered light defined by intensity and angle that can be correlated to a particle size distribution.
  • a number of laser diffraction instruments are commercially available for the rapid and reliable determination of particle size distributions. Unless stated otherwise, particle size distribution measurements as specified or reported herein are as measured by the conventional Malvern Mastersizer TM 3000 particle size analyzer from Malvern Instruments.
  • the Malvern Mastersizer TM 3000 particle size analyzer operates by projecting a helium-neon gas laser beam through a transparent cell containing the particles of interest suspended in an aqueous solution. Light rays which strike the particles are scattered through angles which are inversely proportional to the particle size and a photodetector array measures the intensity of light at several predetermined angles and the measured intensities at different angles are processed by a computer using standard theoretical principles to determine the particle size distribution. Laser diffraction values as reported herein are obtained using a wet dispersion of the particles in distilled water. The particle refractive index is taken to be 3.50 and the dispersant index is taken to be 1.330. Particle size distributions are calculated using the Mie scattering model.
  • the composite particles may have a D 50 particle diameter in the range from 0.5 to 50 ⁇ m.
  • the D 50 particle diameter may be at least 1 ⁇ m, or at least 2 ⁇ m, or at least 3 ⁇ m, or at least 4 ⁇ m, or at least 5 ⁇ m.
  • the D 50 particle diameter may be no more than 40 ⁇ m, or no more than 30 ⁇ m, or no more than 25 ⁇ m, or no more than 20 ⁇ m, or no more than 15 ⁇ m.
  • the composite particles may have a D 50 particle diameter in the range from 1 to 25 ⁇ m, or from 1 to 20 ⁇ m, or from 2 to 20 ⁇ m, or from 2 to 15 ⁇ m, or from 3 to 15 ⁇ m.
  • Particles within these size ranges and having porosity and a pore diameter distribution as set out herein are ideally suited for use in anodes for metal-ion batteries, due to their dispersibility in slurries, their structural robustness, their capacity retention over repeated charge-discharge cycles, and their suitability for forming dense electrode layers of uniform thickness in the conventional range from 20 to 50 ⁇ m.
  • the D 10 particle diameter of the composite particles is preferably at least 0.2 ⁇ m, or at least 0.5 ⁇ m, or at least 0.8 ⁇ m, or at least 1 ⁇ m, or at least 1.5 ⁇ m, or at least 2 ⁇ m.
  • the D 90 particle diameter of the composite particles is preferably no more than 80 ⁇ m, or no more than 60 ⁇ m, or no more than 40 ⁇ m, or no more than 30 ⁇ m, or no more than 25 ⁇ m, or no more than 20 ⁇ m.
  • the presence of very large particles results in non-uniform forming packing of the particles in electrode active layers, thus disrupting the formation of dense electrode layers, particularly electrode layers having a thickness in the range from 20 to 50 ⁇ m. Therefore, it is preferred that the D 90 particle diameter is no more than 40 ⁇ m, and more preferably lower still.
  • the composite particles preferably have a narrow size distribution span.
  • the particle size distribution span (defined as (D 90 -D 10 )/D 50 ) is preferably 5 or less, more preferably 4 or less, more preferably 3 or less, more preferably 2 or less, and most preferably 1.5 or less.
  • the composite particles may be spheroidal in shape.
  • Spheroidal particles as defined herein may include both spherical and ellipsoidal particles and the shape of the composite particles of the invention may suitably be defined by reference to the sphericity and the aspect ratio of the particles of the invention.
  • Spheroidal particles are found to be particularly well-suited to dispersion in slurries without the formation of agglomerates.
  • the use of porous spheroidal particles is surprisingly found to provide a further improvement in strength when compared to porous particles and porous particle fragments of irregular morphology.
  • the sphericity of an object is conventionally defined as the ratio of the surface area of a sphere to the surface area of the object, wherein the object and the sphere have identical volume.
  • SEM scanning electron microscopy
  • dynamic image analysis in which a digital camera is used to record the shadow projected by a particle.
  • the term "sphericity” as used herein shall be understood as the ratio of the area of the particle projection to the area of a circle, wherein the particle projection and circle have identical circumference.
  • the term "spheroidal" as applied to the composite particles of the invention shall be understood to refer to a material having an average sphericity of at least 0.70.
  • the porous spheroidal particles of the invention have an average sphericity of at least 0.85, more preferably at least 0.90, more preferably at least 0.92, more preferably at least 0.93, more preferably at least 0.94, more preferably at least 0.95.
  • the porous spheroidal particles may have an average sphericity of at least 0.96, or at least 0.97, or at least 0.98, or at least 0.99.
  • the circumference and area of a two-dimensional particle projection will depend on the orientation of the particle in the case of any particle which is not perfectly spheroidal.
  • the effect of particle orientation may be offset by reporting sphericity and aspect ratios as average values obtained from a plurality of particles having random orientation.
  • a number of SEM and dynamic image analysis instruments are commercially available, allowing the sphericity and aspect ratio of a particulate material to be determined rapidly and reliably. Unless stated otherwise, sphericity values as specified or reported herein are as measured by a CamSizer XT particle analyzer from Retsch Technology GmbH.
  • the CamSizer XT is a dynamic image analysis instrument which is capable of obtaining highly accurate distributions of the size and shape for particulate materials in sample volumes of from 100 mg to 100 g, allowing properties such as average sphericity and aspect ratios to be calculated directly by the instrument.
  • the composite particles of the invention preferably have a BET surface area of no more than 300 m 2 /g, or no more than 250 m 2 /g, or no more than 200 m 2 /g, or no more than 150 m 2 /g, or no more than 100 m 2 /g, or no more than 80 m 2 /g, or no more than 60 m 2 /g, or no more than 40 m 2 /g, or no more than 30 m 2 /g, or no more than 25 m 2 /g, or no more than 20 m 2 /g, or no more than 15 m 2 /g, or no more than 10 m 2 /g.
  • a low BET surface area is preferred in order to minimise the formation of solid electrolyte interphase (SEI) layers at the surface of the composite particles during the first charge-discharge cycle of an anode comprising the particulate material of the invention.
  • SEI solid electrolyte interphase
  • a BET surface area which is excessively low results in unacceptably low charging rate and capacity due to the inaccessibility of the bulk of the electroactive material to metal ions in the surrounding electrolyte.
  • the BET surface area is preferably at least 0.1 m 2 /g, or at least 1 m 2 /g, or at least 2 m 2 /g, or at least 5 m 2 /g.
  • the BET surface area may be in the range from 1 m 2 /g to 25 m 2 /g, more preferably in the range from 2 to 15 m 2 /g.
  • the particulate material of the invention typically has a specific charge capacity on first lithiation of 1200 to 2340 mAh/g.
  • Preferably the particulate material of the invention has a specific charge capacity on first lithiation of at least 1400 mAh/g.
  • the composite particles of the invention are suitably prepared via the chemical vapor infiltration (CVI) of a silicon-containing precursor into the pore structure of the porous carbon framework.
  • CVI refers to processes in which a gaseous silicon-containing precursor is thermally decomposed on a surface to form elemental silicon at the surface and gaseous by-products.
  • Suitable gaseous silicon-containing precursors include silane (SiH 4 ), silane derivatives (e.g. disilane, trisilane and tetrasilane), and trichlorosilane (SiHCl 3 ).
  • the silicon-containing precursors may be used either in pure form or more usually as a diluted mixture with an inert carrier gas, such as nitrogen or argon.
  • the silicon-containing precursor may be used in an amount in the range from 0.5-20 vol%, or 1-10 vol%, or 1-5 vol% based on the total volume of the silicon-containing precursor and the inert carrier gas.
  • the CVI process is suitably carried out at low partial pressure of silicon precursor with total pressure of 101.3 kPa (i.e.
  • the remaining partial pressure made up to atmospheric pressure using an inert padding gas such as hydrogen, nitrogen or argon.
  • an inert padding gas such as hydrogen, nitrogen or argon.
  • Deposition temperatures ranging from 400-700 °C are used, for example from 400-550 °C, or 400-500 °C, or 400-450 °C, or 450-500 °C.
  • the CVI process may suitably be performed in a fixed bed reactor, fluidized bed reactor (including spouted bed reactor), or rotary kiln.
  • 1.8 g of a particulate porous framework was placed on a stainless-steel plate at a constant thickness of 1 mm along its length.
  • the plate was then placed inside a stainless-steel tube of outer diameter 60 mm with gas inlet and outlet lines located in the hot zone of a retort furnace.
  • the furnace tube was purged with nitrogen gas for 30 minutes at room temperature, then the sample temperature was increased to 450-500 °C.
  • the nitrogen gas flow-rate is adjusted to ensure a gas residence time of at least 90 seconds in the furnace tube and maintained at that rate for 30 minutes. Then, the gas supply is switched from nitrogen to a mixture of monosilane in nitrogen at 1.25 vol. % concentration.
  • Dosing of monosilane is performed over a 5-hour period with a reactor pressure maintained at 101.3 kPa (1 atm). After dosing has finished the gas flow rate is kept constant whilst the silane is purged from the furnace using nitrogen. The furnace is purged for 30 minutes under nitrogen before being cooled down to room temperature over several hours. The atmosphere is then switched over to air gradually over a period of two hours by switching the gas flow from nitrogen to air from a compressed air supply.
  • the particulate material of the invention may optionally include a conductive carbon coating.
  • a conductive carbon coating may be obtained by a chemical vapour deposition (CVD) method.
  • CVD is a well-known methodology in the art and comprises the thermal decomposition of a volatile carbon-containing gas (e.g. ethylene) onto the surface of the particulate material.
  • the carbon coating may be formed by depositing a solution of a carbon-containing compound onto the surface of the particulate material followed by pyrolysis.
  • the conductive carbon coating is sufficiently permeable to allow lithium access to the interior of the composite particles without excessive resistance, so as not to reduce the rate performance of the composite particles.
  • the thickness of the carbon coating may suitably be in the range from 2 to 30 nm.
  • the carbon coating may be porous and/or may only cover partially the surface of the composite particles.
  • a carbon coating has the advantages that it further reduces the BET surface area of the particulate material by smoothing any surface defects and by filling any remaining surface microporosity, thereby further reducing first cycle loss.
  • a carbon coating improves the conductivity of the surface of the composite particles, reducing the need for conductive additives in the electrode composition, and also creates an optimum surface for the formation of a stable SEI layer, resulting in improved capacity retention on cycling.
  • particulate materials according to the following aspects 1-1 to 1-24.
  • Aspect 1-1 A particulate material according to the first aspect of the invention, wherein:
  • a particulate material according to the first aspect of the invention wherein:
  • a particulate material according to the first aspect of the invention wherein:
  • a particulate material according to the first aspect of the invention wherein:
  • Aspect 1-5 A particulate material according to the first aspect of the invention, wherein:
  • a particulate material according to the first aspect of the invention wherein:
  • Aspect 1-7 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-8 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-9 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-10 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-11 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-12 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-13 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-14 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-15 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-16 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-17 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-18 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-19 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-20 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-21 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-22 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-23 A particulate material according to the first aspect of the invention, wherein:
  • Aspect 1-24 A particulate material according to the first aspect of the invention, wherein:
  • a composition comprising a particulate material according to the first aspect of the invention and at least one other component.
  • the particulate material used to prepare the composition of the second aspect of the invention may have any of the features described as preferred or optional with regard to the first aspect of the invention, and may be a particulate material according to any of aspects 1-1 to 1-24.
  • the particulate material of the first aspect of the invention may be used as a component of an electrode composition.
  • compositions comprising a particulate material according to the first aspect of the invention and at least one other component selected from: (i) a binder; (ii) a conductive additive; and (iii) an additional particulate electroactive material.
  • the composition of the invention is useful as an electrode composition, and thus may be used for forming the active layer of an electrode.
  • the electrode composition may be a hybrid electrode composition which comprises a particulate material according to the first aspect of the invention and at least one additional particulate electroactive material.
  • additional particulate electroactive materials include graphite, hard carbon, silicon, germanium, gallium, aluminium and lead.
  • the at least one additional particulate electroactive material is preferably selected from graphite and hard carbon, and most preferably the at least one additional particulate electroactive material is graphite.
  • the at least one additional particulate electroactive material preferably has a D 50 particle diameter in the range from 10 to 50 ⁇ m, preferably from 10 to 40 ⁇ m, more preferably from 10 to 30 ⁇ m and most preferably from 10 to 25 ⁇ m, for example from 15 to 25 ⁇ m.
  • the D 10 particle diameter of the at least one additional particulate electroactive material is preferably at least 5 ⁇ m, more preferably at least 6 ⁇ m, more preferably at least 7 ⁇ m, more preferably at least 8 ⁇ m, more preferably at least 9 ⁇ m, and still more preferably at least 10 ⁇ m.
  • the D 90 particle diameter of the at least one additional particulate electroactive material is preferably no more than 100 ⁇ m, more preferably no more than 80 ⁇ m, more preferably no more than 60 ⁇ m, more preferably no more than 50 ⁇ m, and most preferably no more than 40 ⁇ m.
  • the at least one additional particulate electroactive material is selected from carbon-comprising particles, graphite particles and/or hard carbon particles, wherein the graphite and hard carbon particles have a D 50 particle diameter in the range from 10 to 50 ⁇ m. Still more preferably, the at least one additional particulate electroactive material is selected from graphite particles, wherein the graphite particles have a D 50 particle diameter in the range from 10 to 50 ⁇ m.
  • the particulate material of the invention preferably constitutes from 0.5 to 80 wt% of the total dry weight of the electroactive materials in the electrode composition (i.e. the total dry weight of the particulate material of the invention and the at least one additional particulate electroactive material). More preferably, the particulate material of the invention constitutes from 2 to 70 wt%, more preferably from 4 to 60 wt%, more preferably from 5 to 50 wt% of the total dry weight of the electroactive materials in the electrode composition.
  • the electrode composition may optionally comprise a binder.
  • a binder functions to adhere the electrode composition to a current collector and to maintain the integrity of the electrode composition.
  • binders which may be used in accordance with the present invention include polyvinylidene fluoride (PVDF), polyacrylic acid (PAA) and alkali metal salts thereof, modified polyacrylic acid (mPAA) and alkali metal salts thereof, carboxymethylcellulose (CMC), modified carboxymethylcellulose (mCMC), sodium carboxymethylcellulose (Na-CMC), polyvinylalcohol (PVA), alginates and alkali metal salts thereof, styrene-butadiene rubber (SBR) and polyimide.
  • the electrode composition may comprise a mixture of binders.
  • the binder comprises polymers selected from polyacrylic acid (PAA) and alkali metal salts thereof, and modified polyacrylic acid (mPAA) and alkali metal salts thereof, SBR and CMC.
  • the binder may suitably be present in an amount of from 0.5 to 20 wt%, preferably 1 to 15 wt% and most preferably 2 to 10 wt%, based on the total dry weight of the electrode composition.
  • the binder may optionally be present in combination with one or more additives that modify the properties of the binder, such as cross-linking accelerators, coupling agents and/or adhesive accelerators.
  • the electrode composition may optionally comprise one or more conductive additives.
  • Preferred conductive additives are non-electroactive materials which are included so as to improve electrical conductivity between the electroactive components of the electrode composition and between the electroactive components of the electrode composition and a current collector.
  • the conductive additives may suitably be selected from carbon black, carbon fibers, carbon nanotubes, graphene, acetylene black, ketjen black, metal fibers, metal powders and conductive metal oxides.
  • Preferred conductive additives include carbon black and carbon nanotubes.
  • the one or more conductive additives may suitably be present in a total amount of from 0.5 to 20 wt%, preferably 1 to 15 wt% and most preferably 2 to 10 wt%, based on the total dry weight of the electrode composition.
  • the invention provides an electrode comprising a particulate material as defined with reference to the first aspect of the invention in electrical contact with a current collector.
  • the particulate material used to prepare the electrode of the third aspect of the invention may have any of the features described as preferred or optional with regard to the first aspect of the invention, and may by a particulate material according to any of aspects 1-1 to 1-24.
  • the term current collector refers to any conductive substrate which is capable of carrying a current to and from the electroactive particles in the electrode composition.
  • Examples of materials that can be used as the current collector include copper, aluminium, stainless steel, nickel, titanium and sintered carbon. Copper is a preferred material.
  • the current collector is typically in the form of a foil or mesh having a thickness of between 3 to 500 ⁇ m.
  • the particulate materials of the invention may be applied to one or both surfaces of the current collector to a thickness which is preferably in the range from 10 ⁇ m to 1 mm, for example from 20 to 500 ⁇ m, or from 50 to 200 ⁇ m.
  • the electrode comprises an electrode composition as defined with reference to the second aspect of the invention in electrical contact with a current collector.
  • the electrode composition may have any of the features described as preferred or optional with regard to the second aspect of the invention.
  • the electrode of the third aspect of the invention may suitably be fabricated by combining the particulate material of the invention (optionally in the form of the electrode composition of the invention) with a solvent and optionally one or more viscosity modifying additives to form a slurry.
  • the slurry is then cast onto the surface of a current collector and the solvent is removed, thereby forming an electrode layer on the surface of the current collector. Further steps, such as heat treatment to cure any binders and/or calendaring of the electrode layer may be carried out as appropriate.
  • the electrode layer suitably has a thickness in the range from 20 ⁇ m to 2 mm, preferably 20 ⁇ m to 1 mm, preferably 20 ⁇ m to 500 ⁇ m, preferably 20 ⁇ m to 200 ⁇ m, preferably 20 ⁇ m to 100 ⁇ m, preferably 20 ⁇ m to 50 ⁇ m.
  • the slurry may be formed into a freestanding film or mat comprising the particulate material of the invention, for instance by casting the slurry onto a suitable casting template, removing the solvent and then removing the casting template.
  • the resulting film or mat is in the form of a cohesive, freestanding mass which may then be bonded to a current collector by known methods.
  • the electrode of the third aspect of the invention may be used as the anode of a metal-ion battery.
  • the present invention provides a rechargeable metal-ion battery comprising an anode, the anode comprising an electrode as described above, a cathode comprising a cathode active material capable of releasing and reabsorbing metal ions; and an electrolyte between the anode and the cathode.
  • the particulate material used to prepare the battery of the fourth aspect of the invention may have any of the features described as preferred or optional with regard to the first aspect of the invention, and may be a particulate material according to any of aspects 1-1 to 1-24.
  • the metal ions are preferably lithium ions. More preferably the rechargeable metal-ion battery of the invention is a lithium-ion battery, and the cathode active material is capable of releasing and lithium ions.
  • the cathode active material is preferably a metal oxide-based composite.
  • suitable cathode active materials include LiCoO 2 , LiCo 0.99 Al 0.01 O 2 , LiNiO 2 , LiMnO 2 , LiCo 0.5 Ni 0.5 O 2 , LiCo 0.7 Ni 0.3 O 2 , LiCo 0.8 Ni 0.2 O 2 , LiCo 0.82 Ni 0.18 O 2 , LiCo 0.8 Ni 0.15 Al 0.05 O 2 , LiNi 0.4 Co 0.3 Mn 0.3 O 2 and LiNi 0.33 Co 0.33 Mn 0.34 O 2 .
  • the cathode current collector is generally of a thickness of between 3 to 500 ⁇ m. Examples of materials that can be used as the cathode current collector include aluminium, stainless steel, nickel, titanium and sintered carbon.
  • the electrolyte is suitably a non-aqueous electrolyte containing a metal salt, e.g. a lithium salt, and may include, without limitation, non-aqueous electrolytic solutions, solid electrolytes and inorganic solid electrolytes.
  • a metal salt e.g. a lithium salt
  • non-aqueous electrolyte solutions examples include non-protic organic solvents such as propylene carbonate, ethylene carbonate, butylene carbonates, dimethyl carbonate, diethyl carbonate, gamma butyrolactone, 1,2-dimethoxyethane, 2-methyltetrahydrofuran, dimethylsulfoxide, 1,3-dioxolane, formamide, dimethylformamide, acetonitrile, nitromethane, methylformate, methyl acetate, phosphoric acid triesters, trimethoxymethane, sulfolane, methyl sulfolane and 1,3-dimethyl-2-imidazolidinone.
  • non-protic organic solvents such as propylene carbonate, ethylene carbonate, butylene carbonates, dimethyl carbonate, diethyl carbonate, gamma butyrolactone, 1,2-dimethoxyethane, 2-methyltetrahydrofuran, dimethylsulfoxide, 1,
  • organic solid electrolytes examples include polyethylene derivatives polyethyleneoxide derivatives, polypropylene oxide derivatives, phosphoric acid ester polymers, polyester sulfide, polyvinylalcohols, polyvinylidine fluoride and polymers containing ionic dissociation groups.
  • inorganic solid electrolytes examples include nitrides, halides and sulfides of lithium salts such as Li 5 Ni 2 , Li 3 N, Lil, LiSiO 4 , Li 2 SiS 3 , Li 4 SiO 4 , LiOH and Li 3 PO 4 .
  • the lithium salt is suitably soluble in the chosen solvent or mixture of solvents.
  • suitable lithium salts include LiCI, LiBr, Lil, LiClO 4 , LiBF 4 , LiBCaOs, LiPF 6 , LiCF 3 SO 3 , LiAsF 6 , LiSbF 6 , LiAlCl 4 , CH 3 SO 3 Li and CF 3 SO 3 Li.
  • the metal-ion battery is preferably provided with a separator interposed between the anode and the cathode.
  • the separator is typically formed of an insulating material having high ion permeability and high mechanical strength.
  • the separator typically has a pore diameter of between 0.01 and 100 ⁇ m and a thickness of between 5 and 300 ⁇ m. Examples of suitable electrode separators include a microporous polyethylene film.
  • the separator may be replaced by a polymer electrolyte material and in such cases the polymer electrolyte material is present within both the composite anode layer and the composite cathode layer.
  • the polymer electrolyte material can be a solid polymer electrolyte or a gel-type polymer electrolyte.
  • the invention provides the use of a particulate material as defined with reference to the first aspect of the invention as an anode active material.
  • the particulate material is in the form of an electrode composition as defined with reference to the second aspect of the invention, and most preferably the electrode composition comprises one or more additional particulate electroactive materials as defined above.
  • the particulate material used according to the fifth aspect of the invention may have any of the features described as preferred or optional with regard to the first aspect of the invention, and may be a particulate material according to any of aspects 1-1 to 1-24.
  • Carbon framework particles with the following properties were used to make the particulate composite materials of Table 1:
  • the Si-C composite materials made by the method described herein have the characteristics given in the following Table 1.
  • the silicon-carbon composite materials were synthesized in a vertical bubble-fluidised bed reactor comprising an 83 mm internal diameter stainless steel cylindrical vessel.
  • a 250 g quantity of a powder of carbon framework particles with the properties given above is placed in the reactor.
  • An inert gas (nitrogen) at a low flow rate is injected into the reactor to remove any oxygen.
  • the reactor is then heated to a reaction temperature between 400 and 500°C and 4% v/v monosilane gas diluted in nitrogen is supplied to the bottom of the reactor at a flow rate sufficient to fluidize the carbon framework particles, for a length of time sufficient to deposit the target mass of silicon.
  • Anodes and test cells incorporating the particulate Si-C composite materials of Table 1 were prepared using the following method: Test coin cells were made with negative electrodes comprising the silicon-based material prepared as described above. A dispersion of Carbon Super P (conductive carbon) and in CMC binder was mixed in a Thinky TM mixer. The silicon-based material was added to the mixture and mixed for 30 min in the Thinky TM mixer. SBR binder was then added to give a CMC:SBR ratio of 1:1, yielding a slurry with a weight ratio of silicon-based material: CMC/SBR: conductive carbon set out 70%:16%:14%.
  • the slurry was further mixed for 30 min in the Thinky TM mixer, then was coated onto a 10 ⁇ m thick copper substrate (current collector) and dried at 50 °C for 10 minutes, followed by further drying at 110 °C for 12 hours to thereby form an electrode comprising an active layer on the copper substrate.
  • Full coin cells were made using circular negative electrodes of 0.8 cm radius cut from the electrodes described above with a porous polyethylene separator and a nickel manganese cobalt (NMC532) positive electrode.
  • the positive and negative electrodes were designed to form a balanced pair, such that the projected capacity ratio of the electrodes was around 0.9.
  • An electrolyte comprising 1 M LiPF6 in a 7:3 solution of EMC/FEC (ethylmethyl carbonate/fluoroethylene carbonate) containing 3 wt% vinylene carbonate was then added to the cell before sealing.
  • EMC/FEC ethylmethyl carbonate/fluoroethylene carbonate
  • the full coin cells were cycled as follows: A constant current was applied at a rate of C/25, to lithiate the anode, with a cut off voltage of 4.3 V. When the cut off was reached, a constant voltage of 4.3 V is applied until a cut off current of C/100 is reached. The cell was then rested for 10 minutes in the lithiated state. The anode is then delithiated at a constant current of C/25 with a cut off voltage of 2.75 V. The cell was then rested for 10 minutes. After this initial cycle, a constant current of C/2 was applied to lithiate the anode with a 4.3 V cut off voltage, followed by a 4.3 V constant voltage with a cut off current of C/40 with rest time of 5 minutes. The anode was then delithiated at a constant current of C/2 with a 2.75V cut off. This was then repeated for the desired number of cycles.
  • the charge (lithiation) and discharge (delithiation) capacities for each cycle are calculated per unit mass of the silicon-carbon composite material and the capacity retention value is calculated for each discharge capacity as a % of the discharge capacity on the second cycle.
  • the first cycle loss (FCL) is (1 - (1 st delithiation capacity/1 st lithiation capacity)) ⁇ 100%.
  • FCL first cycle loss

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Claims (15)

  1. Partikelmaterial, umfassend eine Vielzahl von Kompositpartikeln, wobei die Kompositpartikel umfassen:
    (a) ein poröses Kohlenstoffgerüst, umfassend Mikroporen und/oder Mesoporen, wobei die Mikroporen und/oder Mesoporen ein Gesamtporenvolumen, wie gemessen durch Gasadsorption von P1 cm3/g, wobei P1 eine natürliche Zahl mit einem Wert von zumindest 0,7 darstellt, und
    wobei der durch Gasadsorption gemessene PD50-Porendurchmesser nicht mehr als 5 nm beträgt, wobei sich der Begriff PD50-Porendurchmesser auf den volumenbasierten mittleren Porendurchmesser bezieht, basierend auf dem Gesamtvolumen von Mikroporen und Mesoporen; und
    (b) eine Vielzahl von elementaren nanoskaligen Siliziumdomänen innerhalb der Mikroporen und/oder Mesoporen des porösen Kohlenstoffgerüsts;
    wobei das Gewichtsverhältnis von Silizium zu dem porösen Kohlenstoffgerüst in den Kompositpartikeln im Bereich von [0,5×P1 bis 1,3×P1]:1 liegt.
  2. Partikelmaterial nach Anspruch 1, wobei P1 einen Wert im Bereich von 0,8 bis 2,2, oder im Bereich von 0,8 bis 2, oder im Bereich von 0,85 bis 1,8, oder im Bereich von 0,85 bis 1,6, oder im Bereich von 0,9 bis 1,6, oder im Bereich von 0,7 bis 1,5, oder im Bereich von 0,75 bis 1,4, oder im Bereich von 0,75 bis 1,3, oder im Bereich von 0,75 bis 1,2, oder im Bereich von 0,75 bis 1, oder im Bereich von 0,75 bis 0,9 aufweist.
  3. Partikelmaterial nach Anspruch 1 oder Anspruch 2, wobei der PD50-Porendurchmesser des porösen Kohlenstoffgerüsts nicht mehr als 4 nm, oder nicht mehr als 3 nm, oder nicht mehr als 2,5 nm, oder nicht mehr als 2 nm, oder nicht mehr als 1,5 nm, oder nicht mehr als 1 nm beträgt.
  4. Partikelmaterial nach einem vorstehenden Anspruch, wobei der PD90-Porendurchmesser des porösen Kohlenstoffgerüsts nicht mehr als 20 nm, oder nicht mehr als 15 nm, oder nicht mehr als 12 nm, oder nicht mehr als 10 nm, oder nicht mehr als 8 nm, oder nicht mehr als 6 nm, oder nicht mehr als 5 nm, oder nicht mehr als 4 nm, oder nicht mehr als 3 nm, oder nicht mehr als 2,5 nm, oder nicht mehr als 2 nm beträgt, wobei sich der Begriff PD90-Porendurchmesser auf den volumenbasierten 90. Perzentilporendurchmesser bezieht, basierend auf dem Gesamtvolumen von Mikroporen und Mesoporen.
  5. Partikelmaterial nach einem vorstehenden Anspruch, wobei das poröse Kohlenstoffgerüst eine bimodale oder multimodale Porengrößenverteilung relativ zu dem kumulierten gesamten inneren Porenvolumen des porösen Kohlenstoffgerüsts aufweist, bevorzugt einschließlich zumindest eines Gipfelwerts bei weniger als 2 nm und zumindest eines Gipfelwerts im Bereich von 5 bis 50 nm, bevorzugter einschließlich zumindest eines Gipfelwerts bei weniger als 2 nm und zumindest eines Gipfelwerts im Bereich von 10 bis 40 nm.
  6. Partikelmaterial nach einem vorstehenden Anspruch, wobei das Gewichtsverhältnis von Silizium zu dem porösen Kohlenstoffgerüst im Bereich von [0,55×P1 bis 1,1 × P1] : 1 oder im Bereich von [0,6×P1 bis 1,1 × P1] : 1 oder im Bereich von [0,6×P1 bis 1×P1] : 1 oder im Bereich von [0,6×P1 bis 0,95×P1] : 1 oder im Bereich von [0,6×P1 bis 0,9×P1] : 1 oder im Bereich von [0,65×P1 bis 0,9×P1] : 1 oder im Bereich von [0,65×P1 bis 0,85×P1] : 1 oder im Bereich von [0,65×P1 bis 0,8×P1] : 1 oder im Bereich von [0,7×P1 bis 0,8×P1] : 1 liegt.
  7. Partikelmaterial nach einem vorstehenden Anspruch, wobei zumindest ein Teil der Mikroporen und/oder Mesoporen Hohlräume umfasst, welche vollständig von dem Silizium umschlossen sind.
  8. Partikelmaterial nach einem vorstehenden Anspruch, wobei sich zumindest 90 Gew.-%, bevorzugt zumindest 95 Gew.-%, bevorzugter zumindest 98 Gew.-% der Siliziummasse in den Kompositpartikeln innerhalb des inneren Porenvolumens des porösen Kohlenstoffgerüsts befinden.
  9. Partikelmaterial nach einem vorstehenden Anspruch, wobei nicht mehr als 10 %, bevorzugt nicht mehr als 5 %, bevorzugter nicht mehr als 2 % des Siliziumgehalts des Partikelmaterials ist bei 800 °C nicht oxidiert, wenn das Partikelmaterial durch TGA in Luft mit einer Temperaturanstiegsrate von 10°C/min analysiert wird.
  10. Partikelmaterial nach einem vorstehenden Anspruch, wobei die Kompositpartikel einen D50-Partikeldurchmesser im Bereich von 0,5 bis 50 µm, oder von 1 bis 25 µm, oder von 1 bis 20 µm, oder von 2 bis 20 µm, oder von 2 bis 15 µm, oder von 3 bis 15 µm aufweisen, wobei sich D50 auf den volumenbasierten mittleren Partikeldurchmesser bezieht, wie gemessen durch Laserbeugung gemäß ISO 13320:2009.
  11. Partikelmaterial nach einem vorstehenden Anspruch, wobei die Kompositpartikel eine BET-Oberfläche von nicht mehr als 300 m2/g oder nicht mehr als 250 m2/g, oder nicht mehr als 200 m2/g, oder nicht mehr als 150 m2/g, oder nicht mehr als 100 m2/g, oder nicht mehr als 80 m2/g, oder nicht mehr als 60 m2/g, oder nicht mehr als 40 m2/g, oder nicht mehr als 30 m2/g, oder nicht mehr als 25 m2/g, oder nicht mehr als 20 m2/g, oder nicht mehr als 15 m2/g aufweisen.
  12. Zusammensetzung, umfassend ein Partikelmaterial wie in einem der Ansprüche 1-11 definiert und zumindest eine weitere Komponente, optional wobei die zumindest eine weitere Komponente ausgewählt ist aus: (i) einem Bindemittel; (ii) einem leitfähigen Zusatzstoff; und (iii) einem zusätzlichen elektroaktiven Partikelmaterial.
  13. Zusammensetzung nach Anspruch 12, umfassend von 1 bis 95 Gew.-%, oder von 2 bis 90 Gew.-%, oder von 5 bis 85 Gewichtsprozent, oder von 10 bis 80 Gew.-% des Partikelmaterials wie in einem der Ansprüche 1-11 definiert, basierend auf dem gesamten Trockengewicht der Zusammensetzung.
  14. Elektrode, umfassend ein Partikelmaterial wie in einem der Ansprüche 1-11 definiert in elektrischem Kontakt mit einem Stromabnehmer.
  15. Verwendung eines Partikelmaterials wie in einem der Ansprüche 1-11 definiert als aktives Anodenmaterial.
EP19804801.9A 2018-11-08 2019-11-08 Elektroaktive materialien für metall-ionen-batterien Active EP3878033B1 (de)

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GBGB1818232.9A GB201818232D0 (en) 2018-11-08 2018-11-08 Electroactive materials for metal-ion batteries
GB1820736.5A GB2578796B (en) 2018-11-08 2018-12-19 Electroactive materials for metal-ion batteries
US16/274,182 US11011748B2 (en) 2018-11-08 2019-02-12 Electroactive materials for metal-ion batteries
GBGB1912993.1A GB201912993D0 (en) 2018-11-08 2019-09-09 Electroactive materials for metal-ion batteries
PCT/GB2019/053176 WO2020095067A1 (en) 2018-11-08 2019-11-08 Electroactive materials for metal-ion batteries

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